U.S. patent application number 17/295942 was filed with the patent office on 2022-01-13 for high-yield-ratio cold-rolled dual-phase steel and manufacturing method therfor.
This patent application is currently assigned to BAOSHAN IRON & STEEL CO., LTD.. The applicant listed for this patent is BAOSHAN IRON & STEEL CO., LTD.. Invention is credited to Wei LI, Peng XUE, Xiaodong ZHU.
Application Number | 20220010394 17/295942 |
Document ID | / |
Family ID | 1000005914930 |
Filed Date | 2022-01-13 |
United States Patent
Application |
20220010394 |
Kind Code |
A1 |
LI; Wei ; et al. |
January 13, 2022 |
HIGH-YIELD-RATIO COLD-ROLLED DUAL-PHASE STEEL AND MANUFACTURING
METHOD THERFOR
Abstract
Disclosed is a high-yield-ratio cold-rolled dual-phase steel,
having the following chemical elements in percentage by mass:
0.05%-0.08% of C, 0.9%-1.2% of Mn, 0.1%-0.6% of Si, 0.030%4060% of
Nb, 0.030%-0.060% of Ti, 0.015%-0.045% of Al, and the balance being
Fe and other inevitable impurities. A manufacturing method for the
high-yield-ratio cold-rolled dual-phase steel, comprising: (1)
smelting and casting; (2) hot rolling, wherein a casting blank is
controlled and soaked at a temperature of 1200.degree.
C.-1250.degree. C.; rolled with the finish rolling temperature
being 840.degree. C.-930.degree. C.; cooled at a speed of
20.degree. C./s-70.degree. C./s, and then wound at the winding
temperature being 570.degree. C.-630.degree. C.; (3) cold rolling;
(4) annealing at the soaking temperature being 750.degree.
C.-790.degree. C. for 40 s-200 s, cooling at a speed of 30.degree.
C./s-80.degree. C./s, the start temperature of cooling is
650.degree. C. to 730.degree. C., the aging temperature is
200.degree. C. to 260.degree. C., and the overaging time is 100 s
to 400 s; and (5) leveling.
Inventors: |
LI; Wei; (Shanghai, CN)
; ZHU; Xiaodong; (Shanghai, CN) ; XUE; Peng;
(Shanghai, CN) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
BAOSHAN IRON & STEEL CO., LTD. |
Shanghai |
|
CN |
|
|
Assignee: |
BAOSHAN IRON & STEEL CO.,
LTD.
Shanghai
CN
|
Family ID: |
1000005914930 |
Appl. No.: |
17/295942 |
Filed: |
November 22, 2019 |
PCT Filed: |
November 22, 2019 |
PCT NO: |
PCT/CN2019/120247 |
371 Date: |
May 21, 2021 |
Current U.S.
Class: |
1/1 |
Current CPC
Class: |
C21D 8/0236 20130101;
C22C 38/14 20130101; C21D 2211/004 20130101; C21D 2211/005
20130101; C21D 6/008 20130101; C22C 38/06 20130101; C21D 8/0205
20130101; C22C 38/04 20130101; C22C 38/12 20130101; C22C 38/02
20130101; C21D 8/0226 20130101; C21D 2211/008 20130101; C21D 6/005
20130101; C21D 8/0263 20130101; C21D 1/26 20130101 |
International
Class: |
C21D 8/02 20060101
C21D008/02; C21D 6/00 20060101 C21D006/00; C21D 1/26 20060101
C21D001/26; C22C 38/14 20060101 C22C038/14; C22C 38/12 20060101
C22C038/12; C22C 38/06 20060101 C22C038/06; C22C 38/04 20060101
C22C038/04; C22C 38/02 20060101 C22C038/02 |
Foreign Application Data
Date |
Code |
Application Number |
Nov 23, 2018 |
CN |
201811404464.3 |
Claims
1. A cold-rolled dual-phase steel having a high yield ratio,
comprising the following chemical elements in mass percentages: C:
0.05-0.08%, Mn: 0.9-1.2%, Si: 0.1-0.6%, Nb: 0.030-0.060%, Ti:
0.030-0.060%, Al: 0.015-0.045%, and a balance of Fe and other
unavoidable impurities.
2. The cold-rolled dual-phase steel having a high yield ratio
according to claim 1, wherein the steel has a microstructure which
is a complex phase structure of martensite+ferrite+[NbxTiy(C,N)z]
carbonitride.
3. The cold-rolled dual-phase steel having a high yield ratio
according to claim 2, wherein the martensite has a phase proportion
of 20-30%, and the martensite is in the shape of long
strips-islands.
4. The cold-rolled dual-phase steel having a high yield ratio
according to claim 2, wherein the [NbxTiy(C,N)z] carbonitride has
an irregular spherical shape and is uniformly distributed in
ferrite grains, and the [NbxTiy(C,N)z] carbonitride has a phase
proportion of 5-10%.
5. The cold-rolled dual-phase steel having a high yield ratio
according to claim 4, wherein the [NbxTiy(C,N)z] carbonitride has a
size of less than 2 .mu.m.
6. The cold-rolled dual-phase steel having a high yield ratio
according to claim 1, wherein among the other unavoidable
impurities, mass percentages of the P, S and N elements meet at
least one of the following: P.ltoreq.0.015%; S.ltoreq.0.005%;
N.ltoreq.0.005%.
7. The cold-rolled dual-phase steel having a high yield ratio
according to claim 1, wherein the steel has a yield ratio of
greater than 0.8.
8. The cold-rolled dual-phase steel having a high yield ratio
according to claim 7, wherein the steel has a yield strength of
550-660 MPa, a tensile strength of 660 MPa, and an elongation at
break of 15%.
9. A manufacturing method for the cold-rolled dual-phase steel
having a high yield ratio according to claim 1, wherein the method
comprises the following steps: (1) Smelting and casting; (2)
controlling a cast blank for soaking at a temperature of
1200-1250.degree. C.; rolling with a finish rolling temperature
being controlled at 840-930.degree. C.; cooling at a rate of
20-70.degree. C./s after the rolling; then coiling with a coiling
temperature being controlled at 570-630.degree. C.; (3) Cold
rolling; (4) annealing at an annealing soaking temperature of
750-790.degree. C. for an annealing time of 40-200 s; and then
cooling at a rate of 30-80.degree. C./s, wherein the cooling begins
at a temperature of 650-730.degree. C., an aging temperature is
200-260.degree. C., and an over-aging time is 100-400 s; and (5)
Temper rolling.
10. The manufacturing method according to claim 9, wherein in Step
(3), a cold rolling reduction rate is controlled to be 50-70%;
and/or in Step (5), a temper rolling reduction rate is controlled
to be 0.3-1.0%.
11. The manufacturing method according to claim 9, wherein in Step
(2), a soaking time is 5-6 hours; the steel is cooled to 570-630
.degree. C. after the rolling; and then the coiling is
performed.
12. The cold-rolled dual-phase steel having a high yield ratio
according to claim 2, wherein the steel has a yield ratio of
greater than 0.8.
13. The cold-rolled dual-phase steel having a high yield ratio
according to claim 3, wherein the steel has a yield ratio of
greater than 0.8.
14. The cold-rolled dual-phase steel having a high yield ratio
according to claim 4, wherein the steel has a yield ratio of
greater than 0.8.
15. The cold-rolled dual-phase steel having a high yield ratio
according to claim 6, wherein the steel has a yield ratio of
greater than 0.8.
16. The manufacturing method according to claim 9, wherein the
steel has a microstructure which is a complex phase structure of
martensite+ferrite+[NbxTiy(C,N)z] carbonitride.
17. The manufacturing method according to claim 9, wherein the
martensite has a phase proportion of 20-30%, and the martensite is
in the shape of long strips-islands, and/or wherein the
[NbxTiy(C,N)z] carbonitride has an irregular spherical shape and is
uniformly distributed in ferrite grains, and the [NbxTiy(C,N)z]
carbonitride has a phase proportion of 5-10%.
18. The manufacturing method according to claim 17, wherein the
[NbxTiy(C,N)z] carbonitride has a size of less than 2 .mu.m.
19. The manufacturing method according to claim 17, wherein among
the other unavoidable impurities of the cold-rolled dual-phase
steel, mass percentages of the P, S and N elements meet at least
one of the following: P.ltoreq.0.015%; S.ltoreq.0.005%;
N.ltoreq.0.005%.
20. The manufacturing method according to claim 9, wherein the
steel has a yield ratio of greater than 0.8, and or the steel has a
yield strength of 550-660 MPa, a tensile strength of 660 MPa, and
an elongation at break of .gtoreq.15%.
Description
TECHNICAL FIELD
[0001] The present disclosure relates to a steel and a method for
manufacturing the same, in particular to a dual-phase steel and a
method for manufacturing the same.
BACKGROUND ART
[0002] As weight reduction and safety are required in the
automotive industry, the market has an increasing demand for
higher-strength steel plates. Dual-phase steel has excellent
properties such as low yield strength, high tensile strength and
high initial work hardening rate, and is widely used in the
production of automotive parts. In view of the rebound of some
automotive parts such as car seats in practical use, there is a
high demand for 70 kg grade dual-phase steel having a high yield
ratio (a yield ratio of greater than 0.8) in the market.
[0003] In the prior art, a Chinese patent application document
bearing a publication number of 105063510A, a publication date of
Nov. 18, 2015, and a title of "High-plasticity 700 MPa grade
cold-rolled weather-resistant dual-phase steel and preparation
method thereof" discloses a weather-resistant dual-phase steel
having a chemical composition in mass percentages of 0.07-0.15% C,
0.30-0.80% Si, 1.40-1.70% Mn, <0.01% P, <0.01% S, 0.40-0.60%
Cr, 0.20-0.30% Cu, 0.15-0.30% Ni, 0.02-0.05% Nb, 0.02-0.05% Ti, and
a balance of Fe and other unavoidable impurities. The method for
manufacturing the steel plate comprises heat preservation at
1200.degree. C., finish rolling at 950-1050.degree. C., annealing
at 780-820.degree. C., rapid cooling from 660-720.degree. C. at a
rapid cooling rate of 40.degree. C./s, and termination of rapid
cooling at a temperature of 320.degree. C., wherein a 729-747 MPa
steel plate having a yield strength of 328-346 MPa and an
elongation of 21-22% is obtained. In the design of the composition
of the steel plate, relatively large amounts of alloying elements
such as Cr, Cu, Ni are used, and the content of Si is relatively
high.
[0004] Another Chinese patent application document bearing a
publication number of 102766812A, a publication date of Nov. 7,
2012, and a title of "700 MPa grade low yield ratio hot-rolled
dual-phase steel plate and manufacturing method thereof" discloses
a 700 MPa grade low yield ratio hot-rolled dual-phase steel plate
having a chemical composition in mass percentages of 0.06%-0.09% C,
1.0%-1.2% Si, 1.10%-1.30% Mn, 0.020%-0.050% Al, 0.4%-0.6% Cr, and a
balance of Fe. The cast slab used for manufacturing the steel plate
is heated in a heating furnace and rolled through a hot continuous
rolling unit. After rolling, a laminar cooling process is used for
staged cooling, and an ultra-high strength hot-rolled dual-phase
steel having a tensile strength of 700 MPa is obtained at the
end.
[0005] In summary, the dual-phase steel products in the prior art
are mainly classified into two types: (1) cold-rolled, annealed
dual-phase steel plates containing relatively large amounts of such
elements as Cu, Ni, Cr, etc.; and (2) low-yield ratio hot-rolled
steel plates. These two types of products contain relatively large
amounts of alloying elements, while the yield ratio is rather
low.
[0006] In view of this situation, it is desirable to provide a
dual-phase steel that contains less alloying elements and has a
higher yield ratio to meet the market demand for dual-phase steel
having a high yield ratio.
SUMMARY OF THE INVENTION
[0007] One of the objects of the present disclosure is to provide a
cold-rolled dual-phase steel having a high yield ratio, wherein the
dual-phase steel has a low cost, contains less alloying elements,
and has a higher strength and a higher yield ratio, so that it can
satisfy the market demand for dual-phase steel having a high yield
ratio.
[0008] In order to attain the above object, the present disclosure
provides a cold-rolled dual-phase steel having a high yield ratio,
comprising the following chemical elements in mass percentages:
[0009] C: 0.05-0.08%, Mn: 0.9-1.2%, Si: 0.1-0.6%, Nb: 0.030-0.060%,
Ti: 0.030-0.060%, Al: 0.015-0.045%, and a balance of Fe and other
unavoidable impurities.
[0010] In the technical solution of the present disclosure, the
various chemical elements are designed according to the following
principles:
[0011] C: In the high-yield-ratio cold-rolled dual-phase steel of
the present disclosure, carbon is a solid solution strengthening
element which can guarantee the high strength of the material,
increase the strength of martensite, and influence the content of
martensite. If the mass percentage of carbon is too high or too
low, it is disadvantageous to the properties of the steel.
Therefore, the present disclosure limits the mass percentage of the
carbon element in the high-yield-ratio cold-rolled dual-phase steel
to 0.05-0.08%.
[0012] Mn: Manganese is an element that can strongly improve the
hardenability of austenite and effectively increase the strength of
steel, but it is not good for welding. If the mass percentage of Mn
is lower than 0.9%, the strength of the steel will be insufficient;
and if the mass percentage of Mn is higher than 1.2%, the strength
of the steel will be too high. Therefore, the present disclosure
limits the mass percentage of Mn in the high-yield-ratio
cold-rolled dual-phase steel to 0.9-1.2%.
[0013] Si: Silicon is a solid solution strengthening element. On
the one hand, it can increase the strength of the material. On the
other hand, it can accelerate segregation of carbon to austenite,
purify ferrite, and function to improve the elongation of the
steel. At the same time, Si has a great influence on the structure
of the steel. Si tends to accumulate on the surface to form an
oxide film (red rust) that is difficult to remove. If the mass
percentage of Si is less than 0.1%, the strength of the steel will
be insufficient; and if the mass percentage of Si is higher than
0.6%, the surface quality of the steel will be easily affected.
Therefore, the present disclosure limits the mass percentage of Si
in the high-yield-ratio cold-rolled dual-phase steel to
0.1-0.6%.
[0014] Nb: Niobium is an element for precipitation of
carbonitrides. It can refine grains and precipitate carbonitrides
and improve the strength of the material. Therefore, the present
disclosure limits the mass percentage of Nb in the high-yield-ratio
cold-rolled dual phase steel to 0.030-0.060%.
[0015] Ti: Titanium is an element for precipitation of
carbonitrides. It is used for fixing nitrogen and refining grains.
It is conducive to increasing the yield strength of the material.
Therefore, the present disclosure limits the mass percentage of Ti
in the high-yield-ratio cold-rolled dual-phase steel to
0.030-0.060%.
[0016] Al: Al serves to remove oxygen and refine grains in steel.
Therefore, the present disclosure limits the mass percentage of Al
in the high-yield-ratio cold-rolled dual-phase steel to
0.015-0.045%.
[0017] Further, in the cold-rolled dual-phase steel having a high
yield ratio according to the present disclosure, the microstructure
is a complex phase structure of martensite+ferrite+[NbxTiy(C,N)z]
carbonitride.
[0018] Still further, in the cold-rolled dual-phase steel having a
high yield ratio according to the present disclosure, the phase
proportion of the martensite is 20-30%, and the martensite is in
the shape of long strips-islands (it is island-shaped when observed
under a low-magnification metallographic microscope; it is lath or
long strip-shaped when observing the fine structure of the
martensite).
[0019] In the cold-rolled dual-phase steel having a high yield
ratio according to the present disclosure, the phase proportion of
the martensite is 20-30%, and the martensite is in the shape of
long strips-islands. The martensite has a function of phase
transformation strengthening. If the phase proportion of the
martensite is too high or too low, the strength of the steel will
be unduly high or low. Therefore, the present disclosure limits the
phase proportion of the martensite in the cold-rolled dual-phase
steel having a high yield ratio to 20-30%.
[0020] Further, in the cold-rolled dual-phase steel having a high
yield ratio according to the present disclosure, the [NbxTiy(C,N)z]
carbonitride has an irregular spherical shape and is uniformly
distributed in the ferrite grains. The phase proportion of the
[NbxTiy(C,N)z] carbonitride is 5-10%, wherein x+y=z.
[0021] In the cold-rolled dual-phase steel having a high yield
ratio according to the present disclosure, the [NbxTiy(C,N)z]
carbonitride has an irregular spherical shape and is uniformly
distributed in the ferrite grains to achieve dispersion
precipitation strengthening and increase the yield ratio.
[0022] If the phase proportion of the [NbxTiy(C,N)z] carbonitride
is less than 5%, it cannot achieve the effect of increasing the
yield ratio. After the phase proportion of the [NbxTiy(C,N)z]
carbonitride is increased to be higher than 10%, the yield ratio of
the steel will not change much. Therefore, the present disclosure
limits the phase proportion of the [NbxTiy(C,N)z] carbonitride in
the cold-rolled dual-phase steel having a high yield ratio to
5-10%.
[0023] Further, in the cold-rolled dual-phase steel having a high
yield ratio according to the present disclosure, the [NbxTiy(C,N)z]
carbonitride has a size of less than 2 .mu.m.
[0024] Further, in the cold-rolled dual-phase steel having a high
yield ratio according to the present disclosure, among the
unavoidable impurities, the mass percentages of the P, S and N
elements meet at least one of the following: P.ltoreq.0.015%;
S.ltoreq.0.005%; N.ltoreq.0.005%.
[0025] In the cold-rolled dual-phase steel having a high yield
ratio according to the present disclosure, among the unavoidable
impurities, the mass percentages of the P, S and N elements meet at
least one of the following: P.ltoreq.0.015%; S.ltoreq.0.005%;
N.ltoreq.0.005%, according to the following principles:
[0026] P: P is an impurity element in steel. The lower the mass
percentage of P, the better. With the requirements of both the
production cost and process conditions taken into account, the
present disclosure limits the mass percentage of P in the
cold-rolled dual-phase steel having a high yield ratio to
P.ltoreq.0.015%.
[0027] S: S is an impurity element in steel. The lower the mass
percentage of S, the better. With the requirements of both the
production cost and process conditions taken into account, the
present disclosure limits the mass percentage of S in the
cold-rolled dual-phase steel having a high yield ratio to
S.ltoreq.0.005%.
[0028] N: N is an impurity element in steel. If its amount is too
high, the surface of a slab tends to crack. Therefore, the lower
the mass percentage of N, the better. With the requirements of both
the production cost and process conditions taken into account, the
present disclosure limits the mass percentage of N in the
cold-rolled dual-phase steel having a high yield ratio to
N.ltoreq.0.005%.
[0029] Further, the cold-rolled dual-phase steel having a high
yield ratio according to the present disclosure has a yield ratio
of greater than 0.8.
[0030] Further, the cold-rolled dual-phase steel having a high
yield ratio according to the present disclosure has a yield
strength of 550-660 MPa, a tensile strength of .gtoreq.660 MPa, and
an elongation at break of .ltoreq.15%.
[0031] Accordingly, another object of the present disclosure is to
provide a method for manufacturing the above-mentioned cold-rolled
dual-phase steel having a high yield ratio. The cold-rolled
dual-phase steel having a high-yield ratio obtained by this method
has a higher strength and a higher yield ratio.
[0032] To attain the above object, the present disclosure proposes
a method for manufacturing a cold-rolled dual-phase steel having a
high yield ratio, comprising the following steps:
[0033] (1) Smelting and casting;
[0034] (2) Hot rolling: controlling a cast blank for soaking at a
temperature of 1200-1250.degree. C.; rolling with a finish rolling
temperature being controlled at 840-930.degree. C.; cooling at a
rate of 20-70.degree. C./s after the rolling; then coiling with a
coiling temperature being controlled at 570-630.degree. C.;
[0035] (3) Cold rolling;
[0036] (4) Annealing: annealing at an annealing soaking temperature
of 750-790.degree. C. for an annealing time of 40-200 s; and then
cooling at a rate of 30-80.degree. C./s, wherein the cooling begins
at a temperature of 650-730.degree. C., an aging temperature is
200-260.degree. C., and an over-aging time is 100-400 s;
[0037] (5) Temper rolling.
[0038] In the manufacturing method of the present disclosure, in
Step (2), in order to ensure the stability of the rolling load, the
temperature for heating the cast blank is controlled to be
1200.degree. C. or higher. On the other hand, with the solid
solubilities of Ti(C, N) and Nb(C, N)) in austenite taken into
consideration, in order to ensure that the carbonitrides Ti(C,N)
and Nb(C,N) can be precipitated at a high temperature, the upper
limit of the temperature for heating the cast blank is controlled
to be 1250.degree. C. That is, the cast blank is controlled to be
soaked at a temperature of 1200-1250.degree. C., preferably for a
soaking time of 5-6 hours, followed by rolling. In addition, in
view of the formability after the annealing and the possibility
that coarse grains will result in a nonuniform structure, the
finish rolling temperature is controlled to be 840-930.degree. C.
After the rolling, cooling is performed at a rate of 20-70.degree.
C./s, preferably to 570-630.degree. C., and then coiling is
performed. The coiling temperature may be viewed as the
precipitation temperature of the carbonitrides in ferrite, and the
precipitation temperature is one of the main factors that control
the size of the precipitates. The lower the precipitation
temperature, the smaller the critical nucleus size for
precipitation nucleation, and the finer the precipitates. In
addition, the diffusion of Ti and Nb is slow. As a result, the
growth rate of Ti and Nb is also small. From the perspective of
kinetics, due to the high diffusion activation energies of Ti and
Nb, the precipitation process of Ti(C,N) and Nb(C,N) is a result of
long-range diffusion, and full precipitation needs sufficient time.
If the cooling rate is too fast, the precipitation process of the
second phase particles will be inhibited, and at the same time, the
solid solution content will be increased. This is unfavorable for
the precipitation process of Ti(C,N) and Nb(C,N), and the
precipitation amount will be reduced. The coiling temperature is
preferably 570-630.degree. C.
[0039] In addition, in Step (4), the annealing soaking temperature
and annealing time determine the degree of austenitization, and
ultimately determine the phase proportions of martensite and
ferrite in the steel structure. If the annealing soaking
temperature is too high, the phase proportion of martensite will be
so high that the strength of the final steel plate will be unduly
high. If the annealing soaking temperature is too low, the phase
proportion of martensite will be so low that the strength of the
final steel plate will be unduly low. In addition, if the annealing
soaking time is too short, the degree of austenitization will be
insufficient; and if the annealing soaking time is too long, the
austenite grains will become coarse. Therefore, in the
manufacturing method according to the present disclosure, in Step
(4), the annealing soaking temperature is controlled to be
750-790.degree. C.; the annealing time is 40-200 s; and then
cooling is performed at a rate of 30-80.degree. C./s. The starting
temperature of the cooling is 650-730.degree. C.; the aging
temperature is 200-260.degree. C.; and the over-aging time is
100-400 s.
[0040] Further, in the manufacturing method according to the
present disclosure, in Step (3), the cold rolling reduction rate is
controlled to be 50-70%; and/or in Step (5), the temper rolling
reduction rate is controlled to be 0.3-1.0%.
[0041] In the manufacturing method according to the present
disclosure, in Step (3), in some embodiments, the mill scale on the
steel surface may be removed by pickling, and then cold rolling is
performed. In order to produce more polygonal ferrite in the steel
structure, the cold rolling reduction rate is controlled to 50-70%.
In addition, in Step (5), in order to ensure the flatness of the
steel plate, the steel plate needs to be temper rolled to a certain
degree. If it's temper rolled excessively, the yield strength will
increase unduly. Therefore, in the manufacturing method according
to the present disclosure, in Step (5), the temper rolling
reduction rate is controlled to be 0.3-1.0%.
[0042] Compared with the prior art, the cold-rolled dual-phase
steel having a high yield ratio and the manufacturing method
thereof according to the present disclosure have the following
beneficial effects:
[0043] (1) The cold-rolled dual-phase steel having a high yield
ratio according to the present disclosure comprises less alloying
elements (for example, it's free of Cr, Ni, Cu, and the Si content
is also low), has a low cost, and is advantageous for improving the
surface quality and phosphorization property of the cold-rolled
dual-phase steel having a high yield ratio according to the present
disclosure, such that it meets the requirements of automobile
manufacturing.
[0044] (2) The cold-rolled dual-phase steel having a high-yield
ratio according to the present disclosure has a higher strength and
a higher yield ratio as well as a lower carbon equivalent, widely
useful for structural parts and safety parts in the automobile
industry.
[0045] (3) The cold-rolled dual-phase steel having a high yield
ratio according to the present disclosure has a yield ratio of
greater than 0.8, a yield strength of 550-660 MPa, a tensile
strength of .gtoreq.660 MPa, and an elongation at break of
.gtoreq.15%.
[0046] (4) The method for manufacturing the cold-rolled dual-phase
steel having a high yield ratio according to the present disclosure
also has the above-mentioned beneficial effects, which will not be
repeated here.
BRIEF DESCRIPTION OF THE DRAWINGS
[0047] FIG. 1 is a microstructure diagram of a cold-rolled
dual-phase steel having a high yield ratio in Example 2.
DETAILED DESCRIPTION OF THE INVENTION
[0048] The cold-rolled dual-phase steel having a high yield ratio
according to the present disclosure and the method for
manufacturing the same will be further explained and illustrated
with reference to the accompanying drawing of the specification and
the specific examples. Nonetheless, the explanation and
illustration are not intended to unduly limit the technical
solution of the present disclosure.
EXAMPLES 1-6 AND COMPARATIVE EXAMPLES 1-15
[0049] Table 1-1 and Table 1-2 list the mass percentages (wt %) of
the chemical elements in the high-yield-ratio cold-rolled
dual-phase steels of Examples 1-6 and Comparative Examples
1-15.
TABLE-US-00001 TABLE 1-1 (wt %, the balance is Fe and other
unavoidable impurities except for P, S and N) No. C Si Mn P S Nb Ti
Ex. 1 0.052 0.33 1.05 0.014 0.003 0.058 0.044 Ex. 2 0.055 0.18 0.99
0.011 0.004 0.048 0.038 Ex. 3 0.061 0.35 1.17 0.009 0.003 0.042
0.045 Ex. 4 0.066 0.24 1.01 0.012 0.002 0.039 0.036 Ex. 5 0.074
0.18 0.92 0.01 0.001 0.045 0.033 Ex. 6 0.078 0.35 0.98 0.013 0.005
0.034 0.047 Comp. Ex. 1 0.044 0.29 1.08 0.011 0.002 0.044 0.043
Comp. Ex. 2 0.092 0.36 1.12 0.009 0.004 0.038 0.045 Comp. Ex. 3
0.065 0.27 0.78 0.012 0.004 0.043 0.035 Comp. Ex. 4 0.056 0.25 1.26
0.01 0.002 0.037 0.043 Comp. Ex. 5 0.075 0.38 1.08 0.011 0.005
0.025 0.056 Comp. Ex. 6 0.058 0.29 1.19 0.008 0.002 0.065 0.045
Comp. Ex. 7 0.066 0.47 1.11 0.013 0.004 0.038 0.023 Comp. Ex. 8
0.062 0.52 0.96 0.012 0.003 0.055 0.068 Comp. Ex. 9 0.073 0.29 1.08
0.011 0.002 0.044 0.043 Comp. Ex. 10 0.068 0.33 1.06 0.009 0.001
0.041 0.039 Comp. Ex. 11 0.071 0.46 0.95 0.012 0.004 0.036 0.033
Comp. Ex. 12 0.062 0.32 1.05 0.013 0.002 0.032 0.037 Comp. Ex. 13
0.068 0.29 0.99 0.009 0.003 0.039 0.041 Comp. Ex. 14 0.072 0.40
1.12 0.001 0.001 0.048 0.051 Comp. Ex. 15 0.077 0.38 1.15 0.014
0.003 0.043 0.046
TABLE-US-00002 TABLE 1-2 (wt %, the balance is Fe and other
unavoidable impurities except for P, S and N) phase phase phase
proportion of average size of proportion of proportion of
[NbxTiy(C,N)z] [NbxTiy(C,N)z] No. Al N C+(Mn + Si)/6 ferrite (%)
martensite (%) carbonitride (%) carbonitride (.mu.m) Ex. 1 0.021
0.0035 0.282 69.2 24.3 6.5 1.2 Ex. 2 0.033 0.0044 0.250 69.9 22.7
7.4 0.8 Ex. 3 0.028 0.0037 0.314 64.6 28.2 7.2 0.7 Ex. 4 0.042
0.0028 0.274 69.6 21.6 8.8 1.0 Ex. 5 0.038 0.0032 0.257 66.5 24.5
9.0 1.5 Ex. 6 0.017 0.0047 0.300 68.2 26.2 5.6 0.6 Comp. Ex. 1
0.034 0.0028 0.272 77.6 15.6 6.8 0.8 Comp. Ex. 2 0.027 0.0044 0.339
54 38.5 7.5 1.1 Comp. Ex. 3 0.032 0.0037 0.240 79.2 12.5 8.3 0.9
Comp. Ex. 4 0.023 0.0028 0.308 51 41.2 7.8 1.6 Comp. Ex. 5 0.035
0.0042 0.318 70 25.6 4.4 2.8 Comp. Ex. 6 0.042 0.0036 0.305 67.9
18.9 13.2 0.4 Comp. Ex. 7 0.028 0.0042 0.329 74.7 21.5 3.8 3.0
Comp. Ex. 8 0.026 0.0036 0.309 62.8 22.9 14.3 0.5 Comp. Ex. 9 0.034
0.0028 0.301 76.7 16.7 6.6 0.6 Comp. Ex. 10 0.022 0.0029 0.300 55.5
37.4 7.1 3.1 Comp. Ex. 11 0.043 0.0033 0.306 69.4 25.8 4.8 1.0
Comp. Ex. 12 0.041 0.0044 0.290 70.6 24.9 4.5 1.2 Comp. Ex. 13
0.038 0.0022 0.281 74.9 16.8 8.3 0.9 Comp. Ex. 14 0.029 0.0035
0.325 55.6 36.8 7.6 1.5 Comp. Ex. 15 0.030 0.0047 0.332 69.2 24.3
6.5 1.4
[0050] The method for manufacturing the high-yield-ratio
cold-rolled dual-phase steels of Examples 1-6 and Comparative
Examples 1-15 is as follows (the specific process parameters are
listed in Table 2-1 and Table 2-2):
[0051] (1) Smelting and casting: Smelting and casting were carried
out with the chemical elements listed in Table 1-1 and Table
1-2.
[0052] (2) Hot rolling: A cast blank was controlled for soaking at
a temperature of 1200-1250.degree. C. for 5-6 hours, and then
rolled, wherein the finish rolling temperature was controlled at
840-930.degree. C. After the rolling, the steel was cooled at a
rate of 20-70.degree. C./s to 570-630.degree. C. Then, the steel
was coiled, wherein the coiling temperature was controlled at
570-630.degree. C.
[0053] (3) Cold rolling: The cold rolling reduction rate was
controlled at 50-70%.
[0054] (4) Annealing: The annealing soaking temperature was
750-790.degree. C.; and the annealing time was 40-200 s. Then, the
steel was cooled at a rate of 30-80.degree. C./s, wherein the
cooling began at a temperature of 650-730.degree. C. The aging
temperature was 200-260.degree. C., and the over-aging time was
100-400 s.
[0055] (5) Temper rolling: The temper rolling reduction rate was
0.3-1.0%.
TABLE-US-00003 TABLE 2-1 Specific process parameters for the method
for manufacturing the high-yield-ratio cold-rolled dual-phase
steels of Examples 1-6 and Comparative Examples 1-15 Step (2) Step
(3) Soaking Finish Rolling Cooling Coiling Cold Rolling Temperature
Temperature Rate Temperature Reduction Rate No. (.degree. C.)
(.degree. C.) (.degree. C./s) (.degree. C.) (%) Ex. 1 1240 925 40
585 62 Ex. 2 1230 860 30 590 70 Ex. 3 1250 900 60 615 65 Ex. 4 1215
905 55 625 55 Ex. 5 1220 855 50 580 58 Ex. 6 1230 925 30 570 65
Comp. Ex. 1 1230 890 60 595 50 Comp. Ex. 2 1220 875 65 620 64 Comp.
Ex. 3 1200 915 70 580 68 Comp. Ex. 4 1240 845 35 590 56 Comp. Ex. 5
1250 880 30 570 55 Comp. Ex. 6 1200 910 65 620 60 Comp. Ex. 7 1245
860 30 595 62 Comp. Ex. 8 1225 935 45 605 54 Comp. Ex. 9 1190 905
40 590 62 Comp. Ex. 10 1265 900 35 575 50 Comp. Ex. 11 1245 855 60
550 55 Comp. Ex. 12 1220 865 65 640 65 Comp. Ex. 13 1225 895 55 600
68 Comp. Ex. 14 1230 875 45 610 70 Comp. Ex. 15 1240 925 65 585
52
TABLE-US-00004 TABLE 2-2 Specific process parameters for the method
for manufacturing the high-yield-ratio cold-rolled dual-phase
steels of Examples 1-6 and Comparative Examples 1-15 Step (4) Step
(5) Annealing Initial Temper Soaking Cooling Cooling Aging Rolling
Temperature Annealing Rate Temperature Temperature Over-aging
Reduction No. (.degree. C.) Time (s) (.degree. C./s) (.degree. C.)
(.degree. C.) Time (s) Rate (%) Ex. 1 765 40 75 700 230 100 0.8 Ex.
2 780 80 60 660 240 200 0.6 Ex. 3 785 120 55 650 200 400 0.9 Ex. 4
774 160 70 730 250 200 1.0 Ex. 5 782 40 45 670 230 100 0.5 Ex. 6
758 80 70 660 240 300 0.9 Comp. Ex. 1 778 120 45 650 240 300 0.6
Comp. Ex. 2 785 160 50 670 200 400 0.7 Comp. Ex. 3 755 40 60 660
250 200 0.8 Comp. Ex. 4 790 80 55 650 230 100 0.9 Comp. Ex. 5 775
120 35 730 240 300 1.0 Comp. Ex. 6 768 160 80 670 200 400 0.5 Comp.
Ex. 7 786 80 65 670 260 300 0.8 Comp. Ex. 8 766 100 30 660 220 200
0.6 Comp. Ex. 9 775 40 45 720 250 200 0.7 Comp. Ex. 10 785 80 70
700 230 100 0.8 Comp. Ex. 11 768 120 45 680 240 300 0.5 Comp. Ex.
12 755 160 50 650 240 200 0.9 Comp. Ex. 13 745 40 45 695 200 100
1.0 Comp. Ex. 14 805 80 55 705 250 300 0.8 Comp. Ex. 15 774 160 60
730 230 300 1.2
[0056] The high-yield-ratio cold-rolled dual-phase steels of
Examples 1-6 and Comparative Examples 1-15 were tested for their
properties. The test results are listed in Table 3.
TABLE-US-00005 TABLE 3 Yield Tensile Elongation Strength Strength
At Break Yield No. (MPa) (MPa) (%) Ratio Ex. 1 580 690 19.5 0.84
Ex. 2 575 686 18.4 0.84 Ex. 3 604 720 18.2 0.84 Ex. 4 652 764 15.6
0.85 Ex. 5 643 751 15.3 0.86 Ex. 6 628 708 17.5 0.89 Comp. Ex. 1
525 650 21.2 0.81 Comp. Ex. 2 693 790 14.3 0.88 Comp. Ex. 3 508 632
22.6 0.80 Comp. Ex. 4 685 814 13.8 0.84 Comp. Ex. 5 564 754 16.1
0.75 Comp. Ex. 6 632 724 17.6 0.87 Comp. Ex. 7 555 708 18.8 0.78
Comp. Ex. 8 602 697 19.3 0.86 Comp. Ex. 9 532 646 21.8 0.82 Comp.
Ex. 10 683 796 14.1 0.86 Comp. Ex. 11 564 734 17.9 0.77 Comp. Ex.
12 568 727 17.6 0.78 Comp. Ex. 13 565 638 21.7 0.89 Comp. Ex. 14
684 785 14.6 0.87 Comp. Ex. 15 699 774 15.2 0.90
[0057] As can be seen from Table 3, the high-yield-ratio
cold-rolled dual-phase steels of Examples 1-6 and Comparative
Examples 1-15 have a tensile strength of .gtoreq.660 MPa, an
elongation at break of .gtoreq.15%, and a yield ratio of greater
than 0.8. Thus, it can be seen that the cold-rolled dual-phase
steel having a high yield ratio according to the present disclosure
has the advantages of high strength, low carbon equivalent and high
yield ratio.
[0058] FIG. 1 is a microstructure diagram of a cold-rolled
dual-phase steel having a high yield ratio in Example 2.
[0059] As can be seen from FIG. 1, the microstructure of the
high-yield-ratio cold-rolled dual-phase steel of Example 2 is a
complex phase structure of martensite+ferrite+[NbxTiy(C,N)z]
carbonitride, wherein the martensite has a phase proportion of
20-30%, and has a function of phase transformation strengthening.
The martensite structure is in the shape of long strips-islands (it
is island-shaped when observed under a low-magnification
metallographic microscope; it is lath or long strip-shaped when
observing the fine structure of the martensite). Meanwhile, the
[NbxTiy(C,N)z] carbonitride has an irregular spherical shape and is
uniformly distributed in the ferrite grains. The carbonitride has a
size of less than 2 .mu.m, and has a function of dispersion
precipitation strengthening in the structure.
[0060] It's to be noted that the prior art portions in the
protection scope of the present disclosure are not limited to the
examples set forth in the present application file. All the prior
art contents not contradictory to the technical solution of the
present disclosure, including but not limited to prior patent
literature, prior publications, prior public uses and the like, may
all be incorporated into the protection scope of the present
disclosure.
[0061] In addition, the ways in which the various technical
features of the present disclosure are combined are not limited to
the ways recited in the claims of the present disclosure or the
ways described in the specific examples. All the technical features
recited in the present disclosure may be combined or integrated
freely in any manner, unless contradictions are resulted.
[0062] It should also be noted that the above-listed Examples are
only specific embodiments of the present disclosure. Obviously, the
present disclosure is not limited to the above Examples, and
similar changes or modifications can be directly derived from or
easily associated with the disclosure of the present disclosure by
those skilled in the art, and should fall within the protection
scope of the present disclosure.
* * * * *